Surface-coated cutting tool

ABSTRACT

A surface-coated cutting tool according to the present invention includes a coating. The coating includes an α-Al 2 O 3  layer. Each of the α-Al 2 O 3  layers on a side of a rake face and a side of a flank face shows (001) orientation. In the α-Al 2 O 3  layer on the rake face side, a length L R3  of a Σ3 crystal grain boundary exceeds 80% of a length L R3-29  of a Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of a total length L R  of all grain boundaries. In the α-Al 2 O 3  layer on the flank face side, a length L F3  of a Σ3 crystal grain boundary exceeds 80% of a length L F3-29  of a Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of a total length L F  of all grain boundaries. A ratio L R3 /L R3-29  is lower than a ratio L F3 /L F3-29 .

TECHNICAL FIELD

The present invention relates to a surface-coated cutting tool.

BACKGROUND ART

A surface-coated cutting tool having a coating formed on a base material has conventionally been used. For example, Japanese Patent Laying-Open No. 2006-198735 (PTD 1) discloses a surface-coated cutting tool having a coating including an α-Al₂O₃ layer in which a ratio of a Σ3 crystal grain boundary in a Σ3-29 crystal grain boundary is 60 to 80%.

Japanese National Patent Publication No. 2014-526391 (PTD 2) discloses a surface-coated cutting tool having a coating including an α-Al₂O₃ layer in which a length of a Σ3 crystal grain boundary exceeds 80% of a length of a Σ3-29 crystal grain boundary.

CITATION LIST Patent Document

-   PTD 1: Japanese Patent Laying-Open No. 2006-198735 -   PTD 2: Japanese National Patent Publication No. 2014-526391

SUMMARY OF INVENTION Technical Problem

As a ratio of a Σ3 crystal grain boundary in grain boundaries included in an α-Al₂O₃ layer is higher in a coating including the α-Al₂O₃ layer composed of polycrystalline α-Al₂O₃, various characteristics represented by mechanical characteristics improve and hence resistance to wear and resistance to breakage are improved. It is thus expected that a cutting tool is longer in life.

In recent working by cutting, however, a speed and efficiency have become high, load imposed on a cutting tool has increased, and life of the cutting tool has disadvantageously become short. Therefore, further improvement in mechanical characteristics of a coating on the cutting tool and longer life of the cutting tool have been demanded.

The present disclosure was made in view of such circumstances, and an object thereof is to provide a surface-coated cutting tool achieving improved mechanical characteristics of a coating and longer life of the cutting tool.

Solution to Problem

A surface-coated cutting tool according to one embodiment of the present disclosure has a rake face and a flank face, and includes a base material and a coating formed on the base material. The coating includes an α-Al₂O₃ layer, the α-Al₂O₃ layer contains a plurality of crystal grains of α-Al₂O₃, and a grain boundary of the crystal grains includes a CSL grain boundary and a general grain boundary. The α-Al₂O₃ layer on a rake face side shows (001) orientation, and in the α-Al₂O₃ layer on the rake face side, a length L_(R3) of a Σ3 crystal grain boundary in the CSL grain boundary exceeds 80% of a length L_(R3-29) of a Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of a total length L_(R) of all grain boundaries which is a sum of length L_(R3-29) and a length L_(RG) of the general grain boundary. The α-Al₂O₃ layer on a flank face side shows (001) orientation, and in the α-Al₂O₃ layer on the flank face side, a length L_(F3) of a Σ3 crystal grain boundary in the CSL grain boundary exceeds 80% of a length L_(F3-29) of a Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of a total length L_(F) of all grain boundaries which is a sum of length L_(F3-29) and a length L_(FG) of the general grain boundary. A ratio L_(R3)/LR₃₋₂₉ of length L_(R3) to length L_(R3-29) is lower than a ratio L_(F3)/L_(F3-29) of length L_(F3) to length L_(F3-29).

Advantageous Effects of Invention

According to the above, mechanical characteristics of a coating can be improved and life of a cutting tool can further be longer.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a perspective view of a surface-coated cutting tool according to one embodiment of the present disclosure.

FIG. 2 is a cross-sectional view along the line II-II in FIG. 1.

FIG. 3 is a cross-sectional view illustrating a surface-coated cutting tool having a honed cutting edge ridgeline portion.

DESCRIPTION OF EMBODIMENTS

[Description of Embodiments of Present Invention]

Embodiments of the present disclosure will initially be listed and described.

[1] A surface-coated cutting tool according to one embodiment of the present disclosure has a rake face and a flank face, and includes a base material and a coating formed on the base material. The coating includes an α-Al₂O₃ layer, the α-Al₂O₃ layer contains a plurality of crystal grains of α-Al₂O₃, and a grain boundary of the crystal grains includes a CSL grain boundary and a general grain boundary. The α-Al₂O₃ layer on a rake face side shows (001) orientation, and in the α-Al₂O₃ layer on the rake face side, a length L_(R3) of a Σ3 crystal grain boundary in the CSL grain boundary exceeds 80% of a length L_(R3-29) of a Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of a total length L_(R) of all grain boundaries which is a sum of length L_(R3-29) and a length L_(RG) of the general grain boundary. The α-Al₂O₃ layer on a flank face side shows (001) orientation, and in the α-Al₂O₃ layer on the flank face side, a length L_(F3) of a Σ3 crystal grain boundary in the CSL grain boundary exceeds 80% of a length L_(F3-29) of a Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of a total length L_(F) of all grain boundaries which is a sum of length L_(F3-29) and a length L_(FG) of the general grain boundary. A ratio L_(R3)/LR₃₋₂₉ of length L_(R3) to length LR₃₋₂₉ is lower than a ratio L_(F3)/L_(F3-29) of length L_(F3) to length L_(F3-29). This surface-coated cutting tool achieves improved mechanical characteristics of a coating and longer life.

[2] In the surface-coated cutting tool, the CSL grain boundary is constituted of the Σ3 crystal grain boundary, a Σ7 crystal grain boundary, a Σ11 crystal grain boundary, a Σ17 crystal grain boundary, a Σ19 crystal grain boundary, a Σ21 crystal grain boundary, a Σ23 crystal grain boundary, and a Σ29 crystal grain boundary, the length L_(R3-29) is a total sum of lengths of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary in the α-Al₂O₃ layer on the rake face side, and length L_(F3-29) is a total sum of lengths of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary in the α-Al₂O₃ layer on the flank face side.

[3] Preferably, the α-Al₂O₃ layer has a thickness from 2 to 20 μm. The characteristics above are thus most effectively exhibited.

[4] Preferably, the α-Al₂O₃ layer has surface roughness Ra less than 0.2 μm.

Thus, adhesive wear between a work material and a cutting edge of the tool is suppressed and consequently resistance to chipping of the cutting edge is improved.

[5] Preferably, the α-Al₂O₃ layer includes a point where an absolute value for compressive stress is maximal, in a region within 2 μm from a surface side of the coating, and the absolute value for compressive stress at the point is lower than 1 GPa. Thus, breakage of the cutting edge of the tool due to mechanical and thermal fatigue which occurs during an intermittent cutting process is suppressed and consequently reliability of the cutting edge is improved.

[6] Preferably, the coating includes a TiC_(x)N_(y) layer between the base material and the α-Al₂O₃ layer, and the TiC_(x)N_(y) layer contains TiC_(x)N_(y) satisfying atomic ratio relation of 0.6≦x/(x+y)≦0.8. Adhesion between the base material and the α-Al₂O₃ layer is thus improved.

[Details of Embodiments of Present Invention]

A surface-coated cutting tool according to an embodiment of the present invention (hereinafter also denoted as the “present embodiment”) will be described in further detail below with reference to FIGS. 1 to 3.

<Surface-Coated Cutting Tool>

Referring to FIG. 1, a surface-coated cutting tool 10 according to the present embodiment (hereinafter simply denoted as a “tool 10”) has a rake face 1, a flank face 2, and a cutting edge ridgeline portion 3 at which rake face 1 and flank face 2 intersect with each other. Namely, rake face 1 and flank face 2 are surfaces connected to each other with cutting edge ridgeline portion 3 being interposed. Cutting edge ridgeline portion 3 implements a cutting edge tip end portion of tool 10. Such a shape of tool 10 relies on a shape of a base material which will be described later.

Though FIG. 1 shows tool 10 representing a throwaway chip for turning, tool 10 is not limited thereto and the tool can suitably be used as a cutting tool such as a drill, an end mill, a throwaway tip for a drill, a throwaway tip for an end mill, a throwaway tip for milling, a metal saw, a gear cutting tool, a reamer, and a tap.

When tool 10 is implemented as a throwaway chip, tool 10 may or may not have a chip breaker, and cutting edge ridgeline portion 3 may have a sharp edge (a ridge at which a rake face and a flank face intersect with each other) (see FIG. 1), may be honed (a sharp edge provided with R) (see FIG. 3), may have a negative land (beveled), and may be honed and have a negative land.

Referring to FIG. 2, tool 10 has a base material 11 and a coating 12 formed on base material 11. Though coating 12 preferably covers the entire surface of base material 11 in tool 10, a part of base material 11 being not covered with coating 12 or a partially different construction of coating 12 does not depart from the scope of the present embodiment.

<Base Material>

Base material 11 according to the present embodiment has a rake face 11 a, a flank face 11 b, and a cutting edge ridgeline portion 11 c at which rake face 11 a and flank face 11 b intersect with each other. Rake face 11 a, flank face 11 b, and cutting edge ridgeline portion 11 c implement rake face 1, flank face 2, and cutting edge ridgeline portion 3 of tool 10, respectively.

For base material 11, any conventionally known base material of such a kind can be employed. Such a base material is preferably exemplified by cemented carbide (for example, WC-based cemented carbide, which contains not only WC but also Co, or to which a carbonitride of Ti, Ta, or Nb may be added), cermet (mainly composed of TiC, TiN, or TiCN), high-speed steel, ceramics (titanium carbide, silicon carbide, silicon nitride, aluminum nitride, or aluminum oxide), a cubic boron nitride sintered object, or a diamond sintered object. Among these various base materials, in particular, WC-based cemented carbide or cermet (in particular, TiCN-based cermet) is preferably selected. This is because such base materials are particularly excellent in balance between hardness and strength at a high temperature and have characteristics excellent as a base material for the surface-coated cutting tool in applications above.

<Coating>

Coating 12 according to the present embodiment may include other layers so long as it includes an α-Al₂O₃ layer. Examples of other layers can include a TiN layer, a TiCN layer, a TiBNO layer, a TiCNO layer, a TiB₂ layer, a TiAlN layer, a TiAlCN layer, a TiAlON layer, and a TiAlONC layer. An order of layering is not particularly limited.

In the present embodiment, a chemical formula such as “TiN”, “TiCN,” or “TiC_(x)N_(y)” in which an atomic ratio is not particularly specified in the present embodiment does not indicate that an atomic ratio of each element is limited only to “1” but encompasses all conventionally known atomic ratios.

Such a coating 12 according to the present embodiment has a function to improve various characteristics such as resistance to wear and resistance to chipping by covering base material 11.

Coating 12 has a thickness suitably of 3-30 μm (not smaller than 3 μm and not greater than 30 μm; a numerical range expressed with “-” in the present application refers to a range including upper limit and lower limit numeric values) and more preferably of 5-20 μm. When a thickness is smaller than 3 μm, resistance to wear may be insufficient, and when the thickness exceeds 30 μm, peel-off or destruction of coating 12 may occur with high frequency during intermittent working, with application of a large stress between coating 12 and base material 11.

<α-Al₂O₃ Layer>

Coating 12 according to the present embodiment includes an α-Al₂O₃ layer. Coating 12 can include one α-Al₂O₃ layer or two or more α-Al₂O₃ layers.

The α-Al₂O₃ layer contains a plurality of crystal grains of α-Al₂O₃ (aluminum oxide of which crystal structure is of an α type). Namely, this layer is composed of polycrystalline α-Al₂O₃. Normally, these crystal grains have a grain size approximately from 100 to 2000 nm. A “crystal grain boundary” is present between a plurality of crystal grains of α-Al₂O₃.

The crystal grain boundary significantly affects characteristics of a substance such as growth of crystal grains, creep characteristics, diffusion characteristics, electric characteristics, optical characteristics, and mechanical characteristics. Important characteristics to be taken into consideration include, for example, a density of crystal grain boundaries in a substance, a chemical composition of an interface, and a crystallographic texture, that is, a crystal grain boundary plane orientation and crystal misorientation. In particular, a coincidence site lattice (CSL) crystal grain boundary plays a special role. The CSL crystal grain boundary (also simply referred to as a “CSL grain boundary”) is characterized by a multiplicity index E, and is defined as a ratio between a density of sites of crystal lattices of two crystal grains in contact with each other at the crystal grain boundary and a density of sites which coincide with each other when the crystal lattices are superimposed on each other. It has generally been admitted that, in a simple structure, a crystal grain boundary having a low E value tends to have low interface energy and special characteristics. Therefore, control of a ratio of a special crystal grain boundary and a crystal misorientation distribution estimated from a CSL model is considered as important for characteristics of a ceramic coating and a method of improving those characteristics.

A technique based on a scanning electron microscope (SEM) known as electron beam backscattered diffraction (EBSD) has recently appeared and has been used for studies of a crystal grain boundary in a ceramic substance. The EBSD technique is based on automatic analysis of a Kikuchi diffraction pattern generated by backscattered electrons.

A crystallographic orientation of each crystal grain of a substance of interest is determined after indexing of a corresponding diffraction pattern. A texture is analyzed and a grain boundary character distribution (GBCD) is determined relatively easily with EBSD, with the use of commercially available software. Crystal grain boundary misorientation of a sample population having a large interface can be determined by applying EBSD to the interfaces. Misorientation distribution is normally associated with a condition for treatment of a substance. Crystal grain boundary misorientation can be obtained based on a common orientation parameter such as an Euler angle, an angle/axis pair, or a Rodrigues' vector. The CSL model is widely used as a tool for determining characteristics.

The crystal grain boundary in the α-Al₂O₃ layer according to the present embodiment includes the CSL grain boundary and the general grain boundary described above. The CSL grain boundary is constituted of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary. Even when any one or more crystal grain boundaries other than the Σ3 crystal grain boundary are not observed in observation with EBSD, such a case does not depart from the scope of the present embodiment so long as an effect of the present embodiment is exhibited. The general grain boundary refers to crystal grain boundaries other than the CSL crystal grain boundary. Therefore, the general grain boundary refers to a remainder resulting from exclusion of the CSL grain boundary from all grain boundaries of crystal grains of α-Al₂O₃ in observation with EBSD.

The α-Al₂O₃ layer according to the present embodiment satisfies (1) to (4) below.

(1) Each of the α-Al₂O₃ layers on a rake face side and on a flank face side shows (001) orientation.

(2) In the α-Al₂O₃ layer on the rake face side, length L_(R3) of the Σ3 crystal grain boundary exceeds 80% of length L_(R3-29) of the Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of total length L_(R) of all grain boundaries which is a sum of L_(R3-29) and length L_(RG) of the general grain boundary.

(3) In the α-Al₂O₃ layer on the flank face side, length L_(F3) of the Σ3 crystal grain boundary exceeds 80% of length L_(F3-29) of the Σ3-29 crystal grain boundary and is not lower than 10% and not higher than 50% of total length L_(F) of all grain boundaries which is a sum of L_(F3-29) and length L_(FG) of the general grain boundary.

(4) Ratio L_(R3)/L_(R3-29) of length L_(R3) to length L_(R3-29) is lower than ratio L_(F3)/L_(F3-29) of length L_(F3) to length L_(F3-29).

(1) above will be described. The α-Al₂O₃ layer on a side of each surface “showing (001) orientation” herein refers to such a condition that a ratio (an area ratio) of crystal grains (α-Al₂O₃) of which normal direction to a (001) plane is within ±20° with respect to a normal direction to a surface of the α-Al₂O₃ layer (a surface located on a surface side of the coating) is not lower than 50% in the α-Al₂O₃ layer. Specifically, it refers to such a condition that, when a vertical cross-section of the α-Al₂O₃ layer (a cross-section in parallel to the normal direction to the surface of the α-Al₂O₃ layer) on each of the rake face side and the flank face side is observed with an SEM with EBSD and a result thereof is subjected to image processing with color mapping, an area ratio of the above-described crystal grains in the α-Al₂O₃ layer in each observation image subjected to image processing is not lower than 50%.

All areas of the α-Al₂O₃ layer in a direction of thickness are subjected to color mapping of the α-Al₂O₃ layer. Namely, all regions from the surface located on a cover surface side of the α-Al₂O₃ layer to the surface located on a side of the base material of the α-Al₂O₃ layer is subjected to color mapping. All areas in the direction of thickness of the α-Al₂O₃ layer having a thickness of the order of micrometer can be observed in one observation image. On the other hand, any area in an in-plane direction (a direction orthogonal to the direction of thickness) of the α-Al₂O₃ layer should only be subjected to color mapping.

In general, as the α-Al₂O₃ layer is highly oriented in line with the (001) plane, a hardness of the α-Al₂O₃ layer is higher. Therefore, according to the α-Al₂O₃ layer in the present embodiment which satisfies (1), occurrence of a crack due to impact applied during working can be suppressed, toughness of the cutting tool can significantly be improved, and hence high resistance to wear can be achieved.

The “surface side of the coating” means a side opposite to the side of the base material in the direction of thickness of the α-Al₂O₃ layer, and when no other layer is formed on the α-Al₂O₃ layer, it means the surface of the α-Al₂O₃ layer.

(2) and (3) above will be described. The Σ3 crystal grain boundary is considered as lowest in grain boundary energy among CSL crystal grain boundaries of α-Al₂O₃, and hence it is considered that mechanical characteristics (in particular, resistance to plastic deformation) can be enhanced by increasing a ratio thereof in all CSL crystal grain boundaries. Therefore, in the present embodiment, the all CSL crystal grain boundaries are denoted as the Σ3-29 crystal grain boundary, and length L_(R3) of the Σ3 crystal grain boundary in the α-Al₂O₃ layer on the rake face side is defined as exceeding 80% of length L_(R3-29) of the Σ3-29 crystal grain boundary in the α-Al₂O₃ layer on the rake face side and length L_(F3) of the Σ3 crystal grain boundary in the α-Al₂O₃ layer on the flank face side is defined as exceeding 80% of length L_(F3-29) of the Σ3-29 crystal grain boundary in the α-Al₂O₃ layer on the flank face side.

Length L_(R3) refers to a total length of the Σ3 crystal grain boundary in a field of view observed in observation with an SEM with EBSD of the α-Al₂O₃ layer on the rake face side, and length L_(R3-29) refers to the total sum of lengths of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary in a field of view observed in observation with an SEM with EBSD of the α-Al₂O₃ layer on the rake face side. Similarly, length L_(F3) refers to a total length of the Σ3 crystal grain boundary in a field of view observed in observation with an SEM with EBSD of the α-Al₂O₃ layer on the flank face side, and length L_(F3-29) refers to the total sum of lengths of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary in a field of view observed in observation with an SEM with EBSD of the α-Al₂O₃ layer on the flank face side.

Length L_(R3) is more preferably 83% or higher and further preferably 85% or higher of length L_(R3-29). This is also applicable to length L_(F3), and length L_(F3) is more preferably 83% or higher and further preferably 85% or higher of length L_(F3-29). A numeric value is thus preferably as high as possible, and an upper limit thereof does not have to be defined. From a point of view of a thin film being polycrystalline, however, the upper limit is 99% or lower.

Since the Σ3 crystal grain boundary has high conformity as is clear also from the fact that it is low in grain boundary energy, two crystal grains of which grain boundary is defined by the Σ3 crystal grain boundary exhibit a behavior similar to a behavior of a single crystal or twin crystals and tend to be coarser. As crystal grains are coarser, characteristics of a coating such as resistance to chipping lower and hence coarsening should be suppressed. Therefore, in the present embodiment, the suppression effect above is ensured by defining respective lengths L_(R3) and L_(F3) of the Σ3 crystal grain boundary to be not lower than 10% and not higher than 50% of total lengths L_(R) and L_(F) of all grain boundaries in the α-Al₂O₃ layer located on the sides of the rake face and the flank face.

When respective lengths L_(R3) and L_(F3) of the Σ3 crystal grain boundary exceed 50% of total lengths L_(R) and L_(F) of all grain boundaries on the side of respective surfaces, crystal grains unfavorably become coarser, and when the lengths are lower than 10%, excellent mechanical characteristics cannot be obtained. A more preferred range of lengths L_(R3) and L_(F3) of the Σ3 crystal grain boundary is from 20 to 45% and a further preferred range is from 30 to 40%.

All grain boundaries refer to the CSL crystal grain boundary and the general crystal grain boundary other than the CSL crystal grain boundary as being added. Therefore, “total length L_(R) of all grain boundaries” on the side of the rake face can be expressed as the “sum of length L_(R3-29) of the Σ3-29 crystal grain boundary and length L_(RG) of the general grain boundary” and “total length L_(F) of all grain boundaries” on the side of the flank face can be expressed as the “sum of length L_(F3-29) of the Σ3-29 crystal grain boundary and length L_(FG) of the general grain boundary.”

(4) above will be described. The α-Al₂O₃ layer satisfying (4) is relatively high in ratio occupied by the Σ3 crystal grain boundary in the CSL grain boundary in the α-Al₂O₃ layer on the side of the rake face and relatively low in ratio of the Σ3 crystal grain boundary in the CSL grain boundary in the α-Al₂O₃ layer on the side of the flank face. Therefore, the α-Al₂O₃ layer satisfying (2) and (3) and further satisfying (4) is particularly excellent in resistance to plastic deformation on the side of the flank face and can sufficiently suppress lowering in characteristics of the coating such as resistance to chipping attributed to too much Σ3 crystal grain boundary on the side of the rake face.

In a cutting process under a high-speed condition and a low-feed condition (hereinafter also denoted as a “high-speed and low-feed cutting process”), thermal load on the side of the flank face is high and wear of the flank face tends to increase. The α-Al₂O₃ layer satisfying (2) to (4) can withstand load applied to the side of the flank face, and hence long life can be maintained also in the high-speed and low-feed cutting process under severe cutting conditions in particular on the side of the flank face.

A difference {(L_(R3)/L_(R3-29))−(L_(F3)/L_(F3-29))} between ratio L_(R3)/L_(R3-29) and ratio L_(F3)/L_(F3-29) is preferably from −1 to −10. In this case, balance between improvement in resistance to chipping on the side of the rake face and improvement in resistance to plastic deformation on the side of the flank face is excellent. The difference is more preferably from −4 to −9. In order to satisfy such a difference, length L_(R3) of the Σ3 crystal grain boundary is preferably from 80 to 95%, more preferably from 83 to 95%, and particularly preferably from 80 to 90%, of length L_(R3-29) of the Σ3-29 crystal grain boundary. Length L_(F3) of the Σ3 crystal grain boundary is preferably from 90 to 99% and more preferably from 91 to 99% of length L_(F3-29) of the Σ3-29 crystal grain boundary.

In the present embodiment, whether or not the α-Al₂O₃ layer satisfies (1) can be determined as follows.

Initially, an α-Al₂O₃ layer is formed on the base material based on a manufacturing method which will be described later. Then, the formed α-Al₂O₃ layer (including the base material) on the side of the rake face is cut to obtain a cross-section perpendicular to the α-Al₂O₃ layer (that is, cut to expose a cut surface obtained by cutting the α-Al₂O₃ layer along a plane including a normal line to the surface of the α-Al₂O₃ layer). Thereafter, the cut surface is polished with water resistant sandpaper (which contains an SiC grain abrasive as an abrasive).

The α-Al₂O₃ layer is cut, for example, in such a manner that the surface of the α-Al₂O₃ layer (when another layer is formed on the α-Al₂O₃ layer, a surface of the coating) is fixed with the use of wax or the like as being in intimate contact to a sufficiently large flat plate for holding, and thereafter the α-Al₂O₃ layer is cut in a direction perpendicular to the flat plate with a cutter with a rotary blade (cut such that the rotary blade and the flat plate are as perpendicular as possible to each other). Any portion of the α-Al₂O₃ layer can be cut so long as the α-Al₂O₃ layer is cut in such a perpendicular direction.

Polishing is performed successively with water resistant sandpaper #400, #800, and #1500 (the number (#) of the water resistant sandpaper means a difference in grain size of the abrasive, and a greater number indicates a smaller grain size of the abrasive).

In succession, the polished surface is further smoothened through ion milling treatment with the use of Ar ions. Conditions for ion milling treatment are as follows.

Acceleration voltage: 6 kV

Irradiation angle: 0° from a direction of normal to the surface of the α-Al₂O₃ layer (that is, a linear direction in parallel to a direction of thickness of the α-Al₂O₃ layer at the cut surface)

Irradiation time period: 6 hours

A position of cutting is set to avoid at least a portion in the vicinity of cutting edge ridgeline portion 3. Specifically, referring to FIG. 3, a region connecting an outer edge A₁ of a region where a surface in contact with rake face 1 (shown with a dotted line extending laterally in FIG. 3) and rake face 1 are in contact with each other and an outer edge A₂ of a region where a surface in contact with flank face 2 (shown with a dotted line extending vertically in FIG. 3) and flank face 2 are in contact with each other is regarded as cutting edge ridgeline portion 3, and a position distant by 0.2 mm or greater from outer edge A₁ which is an end portion of cutting edge ridgeline portion 3 (a position distant from outer edge A₁ to the left in FIG. 3) is applied as a position of a cross-section. Similarly also in a cross-section on the side of flank face 2 of the α-Al₂O₃ layer, a position distant by 0.2 mm or greater from outer edge A₂ which is an end portion of cutting edge ridgeline portion 3 (a position distant from outer edge A₂ in a downward direction in FIG. 3) is applied as a position of a cross-section.

The smoothened polished surface is observed with an SEM with EBSD. Zeiss Supra 35 VP (manufactured by CARL ZEISS) including an HKL NL02 EBSD detector is employed as the SEM. EBSD data is successively collected by individually positioning focused electron beams onto each pixel.

A normal line to a sample surface (a smoothened cross-section of the α-Al₂O₃ layer) is inclined by 70° with respect to incident beams, and analysis is conducted at 15 kV. In order to avoid a charging effect, a pressure of 10 Pa is applied. A high current mode is set in conformity with a diameter of an opening of 60 μm or 120 μm. Data is collected stepwise at 0.1 μm/step, for 500×300 points corresponding to a plane region of 50×30 m on the polished surface.

Then, with commercially available software (a trademark: “orientation Imaging microscopy Ver 6.2” manufactured by EDAX Inc.), an angle formed between a direction of normal to the (001) plane of each measured pixel and a direction of normal to the surface of the α-Al₂O₃ layer (the surface located on the surface side of the coating) (that is, the linear direction in parallel to the direction of thickness of the α-Al₂O₃ layer at the cut surface) is calculated, and a color map in which a pixel having the angle within ±20° is selected is created.

Specifically, with the technique according to “Crystal Direction MAP” included in the software, a color map of Tolerance of 20° (a difference in direction being within ±20°) between the direction of normal to the surface of the α-Al₂O₃ layer and the direction of normal to the (001) plane of each measured pixel is created. Then, an area ratio of the pixel is calculated based on this color map and the area ratio being 50% or higher is defined as “the α-Al₂O₃ layer on the side of the rake face showing (001) orientation.”

Similarly, whether or not the α-Al₂O₃ layer on the side of the flank face shows (001) orientation is determined. When it is confirmed that the α-Al₂O₃ layer on the side of any surface shows (001) orientation, that is, a ratio of crystal grains (α-Al₂O₃) of which direction of normal to the (001) plane is within ±20° with respect to the direction of normal to the surface (the surface located on the surface side of the coating) of the α-Al₂O₃ layer is not lower than 50%, the α-Al₂O₃ layer satisfies (1).

In the present embodiment, whether or not each of the α-Al₂O₃ layer on the side of the rake face and the α-Al₂O₃ layer on the side of the flank face satisfies (2) and (3) and whether or not it further satisfies (4) can be determined as follows.

Initially, the α-Al₂O₃ layer on the side of the rake face is cut to obtain a cross-section perpendicular to the α-Al₂O₃ layer similarly to the above, and thereafter polishing and smoothing treatment are similarly carried out. Then, the cut surface thus treated is observed with an SEM with EBSD as above.

A normal line to a sample surface (a smoothened cross-section of the α-Al₂O₃ layer) is inclined by 70° with respect to incident beams, and analysis is conducted at 15 kV. In order to avoid a charging effect, a pressure of 10 Pa is applied. A high current mode is set in conformity with a diameter of an opening of 60 μm or 120 μm. Data is collected stepwise at 0.1 μm/step, for 500×300 points corresponding to a plane region of 50×30 m on the polished surface.

Data is processed with and without noise filtering. Noise filtering and crystal grain boundary character distribution are determined by using commercially available software (a trademark: “orientation Imaging microscopy Ver 6.2” manufactured by EDAX Inc.). The crystal grain boundary character distribution is analyzed based on data available from Grimmer (H. Grimmer, R. Bonnet, Philosophical Magazine A 61 (1990), 493-509). With Brandon criterion (ΔΘ<Θ₀ (Σ)^(−0.5), where Θ₀=15°), a tolerance of an experimental value from a theoretical value is taken into account (D. Brandon Acta metall. 14 (1966), 1479-1484). Special crystal grain boundaries corresponding to any Σ value are counted, and the count is expressed as a ratio to all crystal grain boundaries.

As set forth above, length L_(R3) of the Σ3 crystal grain boundary, length L_(R3-29) of the Σ3-29 crystal grain boundary, and total length L_(R) of all grain boundaries in the α-Al₂O₃ layer on the side of the rake face can be found. Similarly, length L_(F3) of the Σ3 crystal grain boundary, length L_(F3-29) of the Σ3-29 crystal grain boundary, and total length L_(F) of all grain boundaries in the α-Al₂O₃ layer on the side of the flank face can be found. Based on the found values, whether or not the α-Al₂O₃ layer on the side of the rake face and the α-Al₂O₃ layer on the side of the flank face satisfy (2) and (3) can be determined and whether or not the α-Al₂O₃ layers further satisfy (4) can be determined.

<Thickness of α-Al₂O₃ Layer>

The α-Al₂O₃ layer preferably has a thickness from 2 to 20 μm. The excellent effect as above can thus be exhibited. The thickness is more preferably from 2 to 15 μm and further preferably from 2 to 10 μm.

When the thickness is smaller than 2 μm, the excellent effect as above may not sufficiently be exhibited. When the thickness exceeds 20 μm, interface stress attributed to a difference in coefficient of linear expansion between the α-Al₂O₃ layer and another layer such as an underlying layer increases and crystal grains of α-Al₂O₃ may come off. Such a thickness can be determined by observing a vertical cross-section of the base material and the coating with a scanning electron microscope (SEM).

<Surface Roughness of α-Al₂O₃ Layer>

The α-Al₂O₃ layer has surface roughness Ra preferably less than 0.2 μm. Thus, not only a coefficient of friction between chips and a cutting edge of a tool lowers and resistance to chipping improves but also stable capability to discharge chips can be exhibited. Surface roughness Ra is more preferably less than 0.15 μm and further preferably less than 0.10 μm. Surface roughness Ra is thus preferably as low as possible, and a lower limit thereof does not have to be defined. From a point of view of the fact that a coating is affected by a surface texture of the base material, however, the lower limit is 0.05 μm or greater.

In the present application, surface roughness Ra means arithmetical mean roughness Ra defined under JIS B 0601 (2001).

<Compressive Stress of α-Al₂O₃ Layer>

The α-Al₂O₃ layer preferably includes a point where an absolute value for compressive stress is maximal, in a region within 2 μm from a surface side of the coating, and the absolute value for compressive stress at the point is lower than 1 GPa. Thus, sudden breakage of a cutting edge due to mechanical and thermal fatigue of the cutting edge of the tool which occurs during an intermittent cutting process is suppressed and a manpower saving/energy saving effect can be exhibited. The absolute value is more preferably lower than 0.9 GPa and further preferably lower than 0.8 GPa. Though the lower limit of the absolute value is not particularly limited, from a point of view of balance between resistance to wear and resistance to breakage, the lower limit is not lower than 0.2 GPa.

Compressive stress in the present embodiment can be measured with the conventionally known sin²ψ method and constant penetration depth method which use X-rays.

<TiC_(x)N_(y) Layer>

The coating according to the present embodiment can include a TiC_(x)N_(y) layer between the base material and the α-Al₂O₃ layer. This TiC_(x)N_(y) layer preferably contains TiC_(x)N_(y) satisfying atomic ratio relation of 0.6≦x/(x+y)≦0.8. Adhesion between the base material and the α-Al₂O₃ layer is thus improved.

The atomic ratio is more preferably 0.65≦x/(x+y)≦0.75 and further preferably 0.67≦x/(x+y)≦0.72. When x/(x+y) is smaller than 0.6, resistance to wear may be insufficient, and when it exceeds 0.8, resistance to chipping may be insufficient.

<Manufacturing Method>

The surface-coated cutting tool according to the present embodiment can be manufactured by forming a coating on a base material through chemical vapor deposition (CVD). When a layer other than the α-Al₂O₃ layer is formed in the coating, such a layer can be formed under conventionally known conditions with the use of a chemical vapor deposition apparatus. The α-Al₂O₃ layer can be formed as below.

AlCl₃, HCl, CO₂, H₂S, O₂, and H₂ are employed as source gases. Amounts of blend of AlCl₃, HCl, CO₂, H₂S, and O₂ are set to 3 to 5 volume %, 4 to 6 volume %, 0.5 to 2 volume %, 1 to 5 volume %, and 0.0001 to 0.01 volume %, respectively, and H₂ is adopted as the remainder. Volume ratios of 0.1≦CO₂/H₂S≦1, 0.1≦CO₂/AlCl₃≦1, and 0.5≦AlCl₃/HCl≦1 are adopted.

Though the source gas is blown to the base material arranged in a reaction vessel in the chemical vapor deposition apparatus, a direction of injection of the source gas is adjusted such that the flank face of the base material is substantially perpendicular to the direction of injection of the source gas and the rake face of the base material is substantially in parallel to the direction of injection of the source gas. Various conditions for chemical vapor deposition include a temperature from 950 to 1050° C., a pressure from 1 to 5 kPa, and a gas flow rate (a total amount of gases) from 50 to 100 L/min. A speed of introduction of the source gas into the reaction vessel is set to 1.7 to 3.5 m/sec.

After the α-Al₂O₃ layer is once formed through chemical vapor deposition under the conditions described above, annealing is performed. Conditions for annealing include a temperature from 1050 to 1080° C., a pressure from 50 to 100 kPa, and a time period from 120 to 300 minutes. An atmosphere for this annealing is obtained by feeding H₂ and argon (Ar) each at a flow rate of 20 to 30 L/min.

The α-Al₂O₃ layer according to the present embodiment having a desired thickness can thus be formed. In particular, by setting an amount of blend of 02 in the source gas to the range above and adjusting a direction of injection of the source gas such that the flank face of the base material is substantially perpendicular to the direction of injection of the source gas and the rake face of the base material is substantially in parallel to the direction of injection of the source gas, the α-Al₂O₃ layer satisfying (2) to (4) can be formed. The reason is estimated as follows.

O₂ is more reactive than other gases such as CO₂, and it has a function to increase the number of nuclei of α-Al₂O₃ or to increase a rate of film formation. O₂ can also have a function to lower a ratio of the Σ3 crystal grain boundary in the CSL crystal grain boundary. This is because generation of the Σ3 crystal grain boundary which is the crystal grain boundary having high conformity is less likely when a rate of film formation is too high.

On the side of the rake face substantially in parallel to the direction of injection of the source gas, a flux density of a source gas tends to relatively be high, and on the side of the flank face substantially perpendicular to the direction of injection of the source gas, a flux density of a source gas tends to be relatively low. Namely, a residence time of a source gas tends to be short on the side of the rake face, and a residence time of a source gas tends to be long on the side of the flank face. In other words, the side of the rake face tends to be supplied with a source gas more frequently than the side of the flank face.

Therefore, apparently, adsorption and diffusion of O₂ on the side of the rake face is more frequent than adsorption and diffusion of O₂ on the side of the flank face, which causes decrease in the Σ3 crystal grain boundary attributed to the function of O₂ on the side of the rake face, and consequently, a ratio of the Σ3 crystal grain boundary on the side of the flank face is higher than on the side of the rake face.

Annealing as above after film formation can prevent an impurity such as sulfur from remaining in the α-Al₂O₃ layer. Therefore, the method of manufacturing the α-Al₂O₃ layer according to the present embodiment is particularly excellent.

EXAMPLES

Though the present invention will be described in further detail below with reference to Examples, the present invention is not limited thereto.

<Preparation of Base Material>

Two types of base materials of a base material P and a base material K shown in Table 1 below were prepared. Specifically, a base material made of cemented carbide and having a shape of CNMG120408NUX (manufactured by Sumitomo Electric Industries, Ltd.) was obtained by uniformly mixing source material powders as formulated as shown in Table 1, forming the powders into a prescribed shape by applying a pressure, and sintering the formed powders for 1 to 2 hours at 1300 to 1500° C.

TABLE 1 Formulated Composition (Mass %) Co Ni TiN TiC Mo₂C TaC WC P 5.0 — 0.5 0.5 — 2.0 Remainder K 4.0 6.0 15.0 Remainder 10.0 — Remainder

<Formation of Coating>

A coating was formed on a surface of each base material obtained as above. Specifically, a coating was formed on the base material through chemical vapor deposition, with the base material being set in a chemical vapor deposition apparatus. The base material was arranged in the reaction vessel such that the rake face was substantially in parallel to a direction of injection of a gas and the flank face was substantially orthogonal to the direction of injection of the gas.

Conditions for forming the coating are as shown in Tables 2 and 3 below. Table 2 shows conditions for forming each layer other than the α-Al₂O₃ layer, and Table 3 shows conditions for forming the α-Al₂O₃ layer. TiBNO and TiCNO in Table 2 represent an intermediate layer in Table 5 which will be described later, and other components correspond to layers except for the α-Al₂O₃ layer in Table 5. The TiC_(x)N_(y) layer is composed of TiC_(x)N_(y) in which an atomic ratio x/(x+y) is set to 0.7.

As shown in Table 3, there are 10 conditions of A to G and X to Z for forming the α-Al₂O₃ layer, and A to G correspond to the conditions in Examples and X to Z correspond to the conditions in Comparative Examples (conventional art). In formation of the α-Al₂O₃ layer, a speed of introduction of a source gas was set to 2 m/sec., and a gas pipe for injection of the source gas was rotated at 2 rpm while the base material was fixed. Only the α-Al₂O₃ layer in Examples formed under conditions A to G was annealed under conditions of 1050° C., 50 kPa, a flow rate of H₂ being set to 20 L/min., and a flow rate of Ar being set to 30 L/min. for an annealing time period shown in Table 3.

For example, formation condition A indicates that the α-Al₂O₃ layer is formed by supplying a source gas composed of 3.2 volume % of AlCl₃, 4.0 volume % of HCl, 1.0 volume % of CO₂, 2 volume % of H₂S, 0.003 volume % of O₂, and remainder H₂ to the chemical vapor deposition apparatus, performing chemical vapor deposition under conditions of a pressure of 3.5 kPa, a temperature of 1000° C., and a flow rate (a total amount of gases) of 70 L/min., and thereafter performing annealing for 180 minutes under the conditions above.

Each layer other than the α-Al₂O₃ layer shown in Table 2 was formed similarly through chemical vapor deposition, except for not performing annealing. The “remainder” in Table 2 indicates that H₂ occupies the remainder of the source gases. The “total amount of gases” indicates a total volume flow rate introduced into the chemical vapor deposition apparatus per unit time, with a gas in a standard condition (0° C. and 1 atmospheric pressure) being defined as the ideal gas (also applicable to the α-Al₂O₃ layer in Table 3). A thickness of each layer was adjusted by adjusting as appropriate a time period for film formation (a rate of film formation of each layer was approximately from 0.5 to 2.0 μm/hour).

TABLE 2 Conditions for Film Formation Pressure Temperature Total Amount of Composition of Source Gas (Volume %) (kPa) (° C.) Gases (L/min) TiN TiCl₄ = 2.0%, N₂ = 39.7%, H₂ = Remainder 50 880 52.5 (Underlying Layer) TiN TiCl₄ = 0.5%, N₂ = 41.2%, H₂ = Remainder 80 980 63.7 (Outermost Layer) TiC_(x)N_(y) TiCl₄ = 2.0%, CH₃CN = 0.7%, 9 800 84.5 C₂H₄ = 1.5%, H₂ = Remainder TiBNO TiCl₄ = 36.7%, BCl₃ = 0.1%, CO = 1.6%, 5 970 54.7 CO₂ = 1.7%, N₂ = 61.7%, H₂ = Remainder TiCNO TiCl₄ = 2.1%, CO = 3.2%, CH₄ = 2.8%, 15 1000 60.8 N₂ = 23.7%, H₂ = Remainder

TABLE 3 Composition of Source Gas Volume Ratio Conditions for Film Formation Annealing (Volume %) CO₂/ CO₂/ AlCl₃/ Pressure Temperature Total Amount of Time AlCl₃ HCl CO₂ H₂S O₂ H₂ H₂S AlCl₃ HCl (kPa) (° C.) Gases (L/min) (min) Example A 3.2 4.0 1.0 2 0.0030 Remainder 0.50 0.3 0.8 3.5 1000 70 180 B 3.5 5.0 0.8 1.8 0.0060 Remainder 0.44 0.2 0.7 3.5 1000 70 180 C 3.0 6.0 0.5 1.6 0.0800 Remainder 0.31 0.2 0.5 3.0 1010 60 120 D 4.4 5.0 1.0 1.1 0.0005 Remainder 0.91 0.2 0.9 4.0 980 75 240 E 5.2 6.0 1.6 2 0.0075 Remainder 0.80 0.3 0.9 3.5 1000 70 180 F 3.8 4.5 2.0 3 0.0009 Remainder 0.67 0.5 0.8 4.0 980 80 300 G 5.0 5.5 1.0 5 0.0100 Remainder 0.20 0.2 0.9 3.0 1020 60 180 Comparative X 10 5.0 15 0.2 — Remainder 75 1.5 2.0 5.0 1050 50 — Example Y 2 2.0 3 0.5 — Remainder 6 1.5 1.0 8.0 1020 55 — Z 2 1.5 6 0.05 — Remainder 120 3.0 1.3 6.0 1020 50 —

<Fabrication of Surface-Coated Cutting Tool>

Surface-coated cutting tools in Examples 1 to 15 and Comparative Examples 1 to 6 shown in Tables 4 and 5 below were each fabricated by forming a coating on the base material under the conditions in Tables 2 and 3.

In Tables 4 and 5, a composition and a thickness of each coating were determined with an SEM-EDX (scanning electron microscope-energy dispersive X-ray spectrometry), and a length of the Σ3 crystal grain boundary, a length of the Σ3-29 crystal grain boundary, and a total length of all grain boundaries of the α-Al₂O₃ layer were determined with the method described above. A ratio (%) of crystal grains (α-Al₂O₃) of which normal direction to the (001) plane is within ±20° with respect to the normal direction to the surface of the α-Al₂O₃ layer (the surface located on the surface side of the coating) in the α-Al₂O₃ layers on the side of the rake face and on the side of the flank face was determined with the method described above.

For example, referring to Table 4, the surface-coated cutting tool in Example 1 has a coating having a total thickness of 24.3 μm formed on the base material, by adopting base material P shown in Table 1 as the base material, forming a TiN layer having a thickness of 1.2 μm as an underlying layer on the surface of base material P under the conditions in Table 2, forming a TiC_(x)N_(y) layer having a thickness of 13.0 μm on the underlying layer under the conditions in Table 2, forming a TiBNO layer having a thickness of 0.7 μm as an intermediate layer on the TiC_(x)N_(y) layer under the conditions in Table 2, fabricating the α-Al₂O₃ layer having a thickness of 8.6 μm on the intermediate layer under the formation condition A in Table 3, and thereafter forming a TiN layer having a thickness of 0.9 μm as an outermost layer under the conditions in Table 2. Blank fields in Table 4 indicate absence of a corresponding layer.

Referring to Table 5, in Example 1, in the α-Al₂O₃ layer on the side of the rake face, length L_(R3) of the Σ3 crystal grain boundary is 89% of length L_(R3-29) of the Σ3-29 crystal grain boundary and 17% of total length L_(R) of all grain boundaries. In the α-Al₂O₃ layer on the side of the flank face, length L_(F3) of the Σ3 crystal grain boundary is 94% of length L_(F3-29) of the Σ3-29 crystal grain boundary and 20% of total length L_(F) of all grain boundaries. A value calculated by subtracting a ratio (L_(F3)/L_(F3-29)) (%) from a ratio (L_(R3)/L_(R3-29)) (%) is shown in a field of “(L_(R3)/L_(R3-29))−(L_(F3)/L_(F3-29))”. Since this value is “-”, it can be seen that ratio L_(R3)/L_(R3-29) is lower than ratio L_(F3)/L_(F3-29). This ca-Al₂O₃ layer shows (001) orientation on the side of the rake face and on the side of the flank face.

Since the α-Al₂O₃ layer in each of Comparative Examples 1 to 6 was formed under the conditions according to the conventional art which are not in accordance with the method of the present invention, this α-Al₂O₃ layer was formed of a crystal texture not exhibiting characteristics as in the present invention (see Table 5).

TABLE 4 Construction of Coating (μm) Type of Base Underlying Layer TiC_(x)N_(y) Intermediate Outermost Layer Total Thickness of Material (TiN layer) Layer Layer α-Al₂O₃ Layer (TiN layer) Coating (μm) Example 1 P 1.2 13.0 TiBNO (0.7) A (8.6) 0.9 24.4 Example 2 P 0.5 13.4 TiBNO (0.6) B (7.1) 1.2 22.8 Example 3 P 0.6 16.0 TiBNO (0.9) C (7.1) 0.6 25.2 Example 4 P 0.6 8.7 TiBNO (0.6) D (5.4) 0.9 16.2 Example 5 P 0.8 8.6 TiCNO (0.7)  E (5.7) 1.0 16.8 Example 6 P 0.7 15.0 TiCNO (0.6)  F (6.6) — 22.9 Example 7 P 0.5 11.2 TiCNO (0.7) G (5.3) 1.1 18.8 Example 8 K 0.8 8.5 TiBNO (0.7) A (3.9) — 13.9 Example 9 K 1.1 5.4 TiBNO (0.7) B (4.2) 1.0 12.4 Example 10 K 0.6 7.3 TiCNO (0.8) C (5.3) 1.3 15.3 Example 11 K 0.8 5.5 TiBNO (0.7) D (2.5) 0.5 10.0 Example 12 K 0.4 5.7 TiBNO (0.5)  E (2.3) 1.0 9.9 Example 13 K 0.5 8.1 TiCNO (0.9)  F (4.6) 0.6 14.7 Example 14 K 0.7 6.4 TiCNO (0.9) G (4.0) 1.1 13.1 Example 15 K 0.6 6.6 TiCNO (1.1) D (4.6) — 12.9 Comparative P 0.6 14.6 TiCNO (0.7) X (7.5) 1.3 24.7 Example 1 Comparative P 0.5 13.7 TiCNO (0.8) Y (7.3) — 22.3 Example 2 Comparative P 0.6 13.5 TiCNO (0.6)  Z (7.9) 1.5 24.1 Example 3 Comparative K 0.6 7.2 TiCNO (0.8) X (4.6) 1.3 14.5 Example 4 Comparative K 0.5 6.8 TiCNO (0.8) Y (4.8) — 12.9 Example 5 Comparative K 0.6 6.0 TiCNO (0.6)  Z (4.8) 1.4 13.4 Example 6

TABLE 5 Ratio of L_(R3)/L_(R3-29) L_(R3)/L_(R) L_(F3)/L_(F3-29) L_(F3)/L_(F) (L_(R3)/L_(R3-29)) − (001) Orientation (%) (%) (%) (%) (L_(F3)/L_(F3-29)) Rake Face Flank Face Example A 89 17 94 20 −5 57 73 B 86 15 92 18 −6 55 62 C 90 18 99 22 −9 60 78 D 83 10 89 13 −6 52 58 E 85 11 91 14 −6 54 60 F 84 12 92 18 −8 72 63 G 95 20 99 21 −4 75 80 Comparative X 75 3 74 5 1 52 50 Example Y 82 5 81 7 1 42 40 Z 50 1 51 2 −1 13 15

<Cutting Test>

Two types of cutting tests below were conducted on the surface-coated cutting tools obtained above. The cutting test below belongs to the high-speed and low-feed cutting process.

<Cutting Test 1>

For the surface-coated cutting tools in Examples and Comparative Examples shown in Table 6 below, under cutting conditions below, a time period of cutting until an amount of wear of the flank face (Vb) reached 0.20 mm was counted and a final form of damage of a cutting edge was observed. Table 6 shows results. A longer time period of cutting indicates better resistance to wear and longer life of the tool.

<Conditions for Cutting>

Work material: Cutting of outer circumference of round rod of SCM435

Peripheral speed: 400 m/min.

Feed rate: 0.1 mm/rev

Cutting depth: 1.0 mm

Coolant: used

TABLE 6 Time Period of Cutting (Minute) Example 1 19 Example 2 20 Example 3 23 Example 4 20 Example 5 21 Example 6 22 Example 7 16 Comparative 10 Example 1 Comparative 13 Example 2 Comparative 6 Example 3

Example 3

As is clear from Table 6, the surface-coated cutting tools in Examples are better in both of resistance to wear and resistance to chipping and longer in life of the tool than the surface-coated cutting tools in Comparative Examples. Namely, it could be confirmed that mechanical characteristics of the coating in the surface-coated cutting tools in Examples were improved.

<Cutting Test 2>

For the surface-coated cutting tools in Examples and Comparative Examples shown in Table 7 below, a time period of cutting until an amount of crater wear (Kt) reached 0.20 mm under cutting conditions below was counted. Table 7 shows results. A longer time period of cutting indicates better resistance to wear and longer life of the tool.

<Conditions for Cutting>

Work material: Cutting of outer circumference of round rod of S55C

Peripheral speed: 300 m/min.

Feed rate: 0.05 mm/rev

Cutting depth: 2.0 mm

Coolant: used

TABLE 7 Time Period of Cutting (Minute) Example 8 21 Example 9 16 Example 10 28 Example 11 22 Example 12 26 Example 13 24 Example 14 17 Example 15 14 Comparative 9 Example 4 Comparative 12 Example 5 Comparative 6 Example 6

As is clear from Table 7, the surface-coated cutting tools in Examples are better in resistance to breakage and longer in life of the tool than the surface-coated cutting tools in Comparative Examples. Namely, it could be confirmed that mechanical characteristics of the coating in the surface-coated cutting tools in Examples were improved.

<Confirmation of Effect of Surface Roughness Ra of α-Al₂O₃ Layer>

Surface roughness Ra of the α-Al₂O₃ layer in the surface-coated cutting tools in Examples 1, 2, and 11 was measured under JIS B 0601 (2001). Table 8 shows results.

Then, surface-coated cutting tools in Examples 1A, 2A, and 11A were fabricated by subjecting the α-Al₂O₃ layer of each surface-coated cutting tool to aerolap treatment under conditions below. Surface roughness Ra of the α-Al₂O₃ layer in the surface-coated cutting tool was measured similarly to the above. Table 8 shows results.

<Conditions for Aerolap Treatment>

Media: elastic rubber media with a diameter of approximately 1 mm, which contain diamond grains having an average grain size of 0.1 μm (a trademark: “MultiCone” manufactured by Yamashita Works Co., Ltd.).

Projection pressure: 0.5 bar

Time period of projection: 30 seconds

Wet/dry: dry

For the surface-coated cutting tools in Examples 1, 1A, 2, 2A, 11, and 11A, a time period of cutting until an amount of wear of the flank face (Vb) reached 0.20 mm under cutting conditions below was counted. Table 8 shows results. A longer time period of cutting indicates stable capability to discharge chips, with a coefficient of friction between chips and the cutting edge of the tool being lower.

<Conditions for Cutting>

Work material: Cutting of outer circumference of round rod of SS400

Peripheral speed: 300 m/min.

Feed rate: 0.1 mm/rev

Cutting depth: 1.0 mm

Coolant: not used

TABLE 8 Surface Roughness Time Period of Ra (μm) Cutting (Minute) Example 1 0.33 27 Example 1A 0.12 40 Example 2 0.30 30 Example 2A 0.10 53 Example 11 0.28 35 Example 11A 0.10 60

As is clear from Table 8, it could be confirmed that the surface-coated cutting tools in Examples 1A, 2A, and 11A including the α-Al₂O₃ layer having surface roughness Ra less than 0.2 μm could achieve lowering in coefficient of friction between chips and the cutting edge of the tool and exhibited stable capability to discharge chips, as compared with the surface-coated cutting tools in Examples 1, 2, and 11 including the α-Al₂O₃ layer having surface roughness Ra equal to or more than 0.2 μm.

<Confirmation of Effect of Compressive Stress Provided to α-Al₂O₃ Layer>

For the surface-coated cutting tools in Examples 1, 2, and 11, it was confirmed that there was a point where an absolute value for stress was maximal, in a region within 2 μm from the surface side of the coating in the α-Al₂O₃ layer, and the absolute value of stress at that point was measured. Table 9 shows results (in a field of “stress value”). Stress was measured with the sin²ψ method using X-rays, and a numeric value in the field of “stress value” in Table 9 shows an absolute value, with tensile stress being denoted as “tensile” and compressive stress being denoted as “compressive”.

Then, surface-coated cutting tools in Examples 1B, 1C, 2B, 2C, and 11B were fabricated by subjecting the α-Al₂O₃ layer of each surface-coated cutting tool to wet blast treatment under conditions below. Then, for each surface-coated cutting tool, similarly to the above, it was confirmed that there was a point where an absolute value of stress was maximal, in a region within 2 μm from the surface side of the coating in the α-Al₂O₃ layer, and the absolute value of stress at that point was measured. Table 9 shows results (in a field of “stress value”). Difference in stress between Example 1B and Example 1C and between Example 2B and Example 2C is attributed to a difference in projection pressure in wet blast treatment.

<Conditions for Wet Blast Treatment>

Media: alumina media (φ50 μm)

Projection pressure: 1 to 2 bars

Time period of projection: 10 seconds

Wet/dry: Wet

A time period of cutting until the tool is broken under conditions for cutting below was counted for the surface-coated cutting tools in Examples 1, 1B, 1C, 2, 2B, 2C, 11, and 11B. Table 9 shows results. A longer time period of cutting indicates suppression of breakage of the cutting edge of the tool due to mechanical and thermal fatigue which occurs during an intermittent cutting process and resultant improvement in reliability of the cutting edge.

<Conditions for Cutting>

Work material: SUS304 (cutting of outer circumference of 60°×3 grooves)

Peripheral speed: 250 m/min.

Feed rate: 0.05 mm/rev

Cutting depth: 1.0 mm

Coolant: not used

TABLE 9 Time Period of Stress Value (GPa) Cutting (Minute) Example 1 0.7 (Tensile) 12 Example 1B 0.8 (Compressive) 22 Example 1C 1.0 (Compressive) 20 Example 2 0.8 (Tensile) 10 Example 2B 0.6 (Compressive) 20 Example 2C 0.2 (Compressive) 14 Example 11 0.6 (Tensile) 15 Example 11B 0.8 (Compressive) 27

As is clear from Table 9, it could be confirmed that a point where the absolute value of stress was maximal was included in the region within 2 μm from the surface side of the coating in the α-Al₂O₃ layer, breakage of the cutting edge of the tool due to mechanical and thermal fatigue which occurred during an intermittent cutting process was suppressed in a case that stress at that point was compressive stress of which absolute value was smaller than 1 GPa as compared with a case that stress at that point was tensile stress, and consequently reliability of the cutting edge improved.

Though the embodiment and the examples of the present invention have been described above, combination of features in each embodiment and example described above as appropriate and various modifications thereof are also originally intended.

It should be understood that the embodiment disclosed herein is illustrative and non-restrictive in every respect. The scope of the present invention is defined by the terms of the claims, rather than the embodiment above, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.

REFERENCE SIGNS LIST

1 rake face; 2 flank face; 3 cutting edge ridgeline portion; 10 tool; 11 base material; 11 a rake face; 11 b flank face; 11 c cutting edge ridgeline portion; and 12 coating. 

1. A surface-coated cutting tool having a rake face and a flank face, comprising: a base material; and a coating formed on the base material, the coating including an α-Al₂O₃ layer, the α-Al₂O₃ layer containing a plurality of crystal grains of α-Al₂O₃, a grain boundary of the crystal grains including a CSL grain boundary and a general grain boundary, the α-Al₂O₃ layer on a rake face side showing (001) orientation, in the α-Al₂O₃ layer on the rake face side, a length L_(R3) of a Σ3 crystal grain boundary in the CSL grain boundary exceeding 80% of a length L_(R3-29) of a Σ3-29 crystal grain boundary and being not lower than 10% and not higher than 50% of a total length L_(R) of all grain boundaries which is a sum of the length L_(R3-29) and a length L_(RG) of the general grain boundary, the α-Al₂O₃ layer on a flank face side showing (001) orientation, in the α-Al₂O₃ layer on the flank face side, a length L_(F3) of a Σ3 crystal grain boundary in the CSL grain boundary exceeding 80% of a length L_(F3-29) of a Σ3-29 crystal grain boundary and being not lower than 10% and not higher than 50% of a total length LF of all grain boundaries which is a sum of the length L_(F3-29) and a length L_(FG) of the general grain boundary, and a ratio L_(R3)/L_(R3-29) of the length L_(R3) to the length L_(R3-29) being lower than a ratio L_(F3)/L_(F3-29) of the length L_(F3) to the length L_(F3-29), and the (001) orientation being defined as such a condition that a ration of the crystal grains of α-Al₂O₃ of which normal direction to a (001) planes is within +20° with respect to a normal direction to a surface of the α-Al₂O₃ layer is not lower than 50% in the α-Al₂O₃ layer.
 2. The surface-coated cutting tool according to claim 1, wherein the CSL grain boundary is constituted of the Σ3 crystal grain boundary, a Σ7 crystal grain boundary, a Σ11 crystal grain boundary, a Σ17 crystal grain boundary, a Σ19 crystal grain boundary, a Σ21 crystal grain boundary, a Σ23 crystal grain boundary, and a Σ29 crystal grain boundary, the length L_(R3-29) is a total sum of lengths of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary in the α-Al₂O₃ layer on the rake face side, and the length L_(F3-29) is a total sum of lengths of the Σ3 crystal grain boundary, the Σ7 crystal grain boundary, the Σ11 crystal grain boundary, the Σ17 crystal grain boundary, the Σ19 crystal grain boundary, the Σ21 crystal grain boundary, the Σ23 crystal grain boundary, and the Σ29 crystal grain boundary in the α-Al₂O₃ layer on the flank face side.
 3. The surface-coated cutting tool according to claim 1, wherein the α-Al₂O₃ layer has a thickness from 2 to 20 μm.
 4. The surface-coated cutting tool according to claim 1, wherein the α-Al₂O₃ layer has surface roughness Ra less than 0.2 μm.
 5. The surface-coated cutting tool according to claim 1, wherein the α-Al₂O₃ layer includes a point where an absolute value for compressive stress is maximal, in a region within 2 μm from a surface side of the coating, and the absolute value for compressive stress at the point is lower than 1 GPa.
 6. The surface-coated cutting tool according to claim 1, wherein the coating includes a TiC_(x)N_(y) layer between the base material and the α-Al₂O₃ layer, and the TiC_(x)N_(y) layer contains TiC_(x)N_(y) satisfying atomic ratio relation of 0.6≦x/(x+y)≦0.8. 